CN110699605B - Heat treatment method for reducing residual stress of hot-rolled strip steel - Google Patents
Heat treatment method for reducing residual stress of hot-rolled strip steel Download PDFInfo
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Abstract
The invention relates to a heat treatment method for reducing residual stress of hot-rolled strip steel, which comprises the following steps of heating the hot-rolled strip steel to a temperature above an Ac3 temperature line, and after the steel plate is completely austenitized, performing salt bath quenching treatment on the steel plate, wherein the temperature is kept below an Ms temperature line; then, heating the temperature to be above the Ms temperature line, performing carbon distribution, simultaneously performing vibration treatment on the carbon distribution by using a vibration exciter, and then performing water quenching to room temperature; then, carrying out cryogenic treatment, taking out the steel plate, placing the steel plate in a heat medium for heat preservation for a period of time, and repeating the process once; and finally, putting the steel plate into a heat medium for tempering treatment to obtain a final product. The process can obviously reduce the residual stress of the hot-rolled strip steel and enhance the stability of the material in the service process.
Description
Technical Field
The invention relates to a heat treatment method for reducing residual stress of hot-rolled strip steel.
Technical Field
The hot rolled strip steel is an important industrial raw material in various manufacturing industries, is widely applied to the industries of automobiles, buildings, transportation, chemical industry, electromechanics, mechanical manufacturing and the like, and has higher requirements on the quality and the mechanical property due to the wide demand of the market on the hot rolled strip steel. TMCP (thermo-Mechanical Control Process) is a technology for controlling rolling and cooling, and the specification, quality, Mechanical property and dimensional precision of a steel plate produced by the technology have good effects, and the TMCP is widely applied to various fields for producing hot-rolled strip steel and is one of the biggest contributions of the 20 th century China steel industry.
However, the steel sheet inevitably generates macroscopic residual stress, especially thermal stress and transformation stress during rolling and cooling, and the stress distribution is not uniform due to the fast cooling speed of the steel sheet during cooling or the non-uniform heat dissipation of local areas of the steel sheet, which causes the temperature distribution in the thickness or width direction of the steel sheet to be non-uniform. Residual stresses are generally harmful, in particular in the state of tensile stress at the surface, and have a considerable influence on the engineering properties of materials and structural components, in particular fatigue life, deformation, dimensional stability, corrosion resistance, wear resistance and brittle fracture. Methods for reducing residual stress can be broadly divided into three categories: firstly, a heat treatment method comprises annealing and tempering, but the tempering or the annealing is carried out after quenching, the stress relief effect is poor, and the reduction rate is only 10-35%; secondly, mechanical treatment methods, such as an explosion method and a hammering method, have higher requirements on the process and cause serious damage to workpieces. And thirdly, the electromagnetic regulation and control method, such as a pulse current method and a magnetic pulse method, has a relatively limited application range, relatively high requirements on workpieces and high technical difficulty.
Disclosure of Invention
The invention relates to a heat treatment method for eliminating residual stress of hot-rolled strip steel, which comprises the following elements in percentage by mass: 0.06-0.30%, Si: 0.1-1.5%, Mn: 0.4% -2.0%, Cr: 0.01 to 0.1 percent of Ti: 0.02% -0.12%, Ni: 0.01 to 0.03 percent, and the balance of Fe, trace elements B, V, Mo, S, P and other inevitable impurity elements, and is characterized by comprising the following steps:
step one salt bath quenching treatment
Heating the hot-rolled strip steel to a temperature above an Ac3 temperature line, and after the steel plate is completely austenitized, performing salt bath quenching treatment on the steel plate, wherein the temperature is kept below an Ms temperature line;
step two carbon distribution-vibration treatment
Heating the temperature to be above the Ms temperature line, performing carbon distribution, simultaneously performing vibration treatment on the carbon distribution by using a vibration exciter, and then performing water quenching to room temperature;
three-step cold and hot circulation treatment
Placing the steel plate obtained in the step two into a cooling medium for cryogenic treatment, then taking out the steel plate, placing the steel plate into a heat medium for heat preservation, and repeating the steps once;
step four tempering
And (4) putting the steel plate obtained in the third step into a heat medium for tempering treatment to obtain a final product.
The heat treatment method for reducing the residual stress of the hot-rolled strip steel comprises the following steps that in the first step, the austenitizing temperature of a steel plate is 900-1000 ℃, the heat preservation time is 5-20 min, the salt bath quenching temperature is 300-400 ℃, and the heat preservation time is 5-25 s.
The invention relates to a heat treatment method for reducing residual stress of hot-rolled strip steel, in the second step, the temperature in the carbon distribution process is 400-500 ℃, the heat preservation time is 200-300 s, and the heat treatment method is simultaneously carried out by using a vibration exciter, the selection of the exciting force is related to the self residual stress level of the alloy and the yield stress of the material, and the dynamic stress value is as follows:
σd＝Aexp(B/T)±5
wherein T is the temperature of the medium where the steel plate is located during vibration, A, B are coefficients, A ranges from 43 to 150, B ranges from 10 to 16, and both the coefficient A and the coefficient B are the yield coefficientThe strength-related constant, ± 5, represents the deviation range under the formula, a ═ 2-2.5) exp ^ ln [ (σ ^ 5)s-0.1213B)/15]，σsThe invention is suitable for the material with the yield strength at room temperature of 900Mpa more than or equal to sigmasMore than or equal to 350Mpa and the vibration temperature T is less than or equal to 560 ℃.
The heat treatment method for reducing the residual stress of the hot-rolled strip steel comprises the third step of reducing the temperature of a steel plate to a range of-160 ℃ to-196 ℃ at a speed of 3 ℃/min to 5 ℃/min, preserving the heat for 1h to 2h, taking out the steel plate, placing the steel plate into an air furnace, preserving the heat for 30 min to 60min at a temperature of 150 ℃ to 250 ℃.
In the third step, the cooling medium used for the cryogenic treatment is at least one of liquid nitrogen and dry ice.
The heat treatment method for eliminating the residual stress of the hot-rolled strip steel comprises the fourth step of carrying out low-temperature tempering treatment on a steel plate, wherein the heat preservation interval is 250-500 ℃, and the heat preservation time is 1-2 hours.
Compared with the traditional process, the method has the characteristics that:
1. the method for selecting the dynamic stress of the vibration exciter reflects the relation between the temperature and the dynamic stress, and presents an exponential function relation, because the yield stress of a steel plate is reduced along with the rise of the temperature, and the higher the temperature is under the condition that the yield stress of a material is changed, the smaller the required dynamic stress value is, so that the change of the yield stress and the exciting force is maintained on the same level, the residual stress can be reduced or homogenized more quickly, the yield strengths of different materials are different, and the method is suitable for the materials with the room-temperature yield strength of 900Mpa more than or equal to sigmasMore than or equal to 350Mpa and the vibration temperature T is less than or equal to 560 ℃.
2. According to the carbon distribution-vibration treatment process, vibration treatment at high temperature can accelerate diffusion and migration of carbon atoms or other atoms under the condition that an exciting force is taken as power, solute atoms C in crystals are diffused into an austenite structure of a face-centered cubic from martensite of a body-centered cubic structure, and the crystal structure with the carbon atoms distributed preferentially inevitably generates local plastic deformation along with deformation of a crystal lattice and a whole sample so as to release residual stress; under the action of exciting force, the dislocation state in the material is changed, the dislocation is continuously accumulated and started, along with the continuous increase of the dislocation density and the entanglement of the dislocation, and in a high-temperature environment, enough energy is provided for the atoms in the material, so that the atoms are separated from the dislocation in violent motion and return to a stable equilibrium position, thereby reducing lattice distortion and releasing residual stress. The cooperation of carbon distribution and vibration processing for in the environment of high temperature, the diffusion of carbon atom is more abundant, makes the material produce directional plastic deformation, and dislocation motion aggravation makes the higher position of residual stress in the sample at first get into the yield stage, thereby produces corresponding local small plastic deformation, thereby reduces residual stress's effect. In the process, the elimination effect of the residual stress is obviously improved under the condition of ensuring the strength of the process by the synergistic action of the carbon distribution process and the vibration treatment, and compared with the conventional quenching-carbon distribution heat treatment process, the reduction rate is up to 62 percent and the minimum rate is up to 48.8 MPa.
3. According to the carbon distribution-vibration treatment process provided by the invention, because the quenching temperature of the first salt bath quenching is below the Ms temperature line, the martensite content is less when the quenching temperature is close to the Ms line, the thermal stress in the process occupies the dominant position, and a certain exciting force is applied to the hot rolled strip steel in the carbon distribution-vibration treatment process, so that the kinetic energy of carbon atoms is increased, the motion range of the carbon atoms and microdefects is enlarged, and dislocation is subjected to deposition, starting and proliferation under the action of an external cyclic load, and the density of point defects is reduced, so that the microstructure distribution is homogenized; dislocation slips and is greatly multiplied, and residual stress is released. The thermal stress generated in the original primary salt bath quenching process is expressed as a state of external pulling and internal pressure, so that the residual stress on the surface and the center is gradually reduced in the carbon distribution-vibration treatment process, and the reduction effect is obvious.
4. The invention carries out short-time cold-hot circulation treatment process after carbon distribution-vibration treatment, the subzero treatment is usually used for improving other mechanical properties such as the wear resistance of steel, and the like, because the alloy steel is precipitated along with carbide in the process of the subzero treatment, unstable residual austenite is converted into martensite in the process of the subzero treatment, and the surface of the steel plate is in a pressed state due to the surface expansion caused by the phase change of the low-density martensite in the austenite, and is superposed with the residual stress field in the previous carbon distribution-vibration treatment process, thereby achieving the effect of reducing the residual stress; compared with a long-time subzero treatment, the short-time cold-hot circulation process has the advantages that precipitated carbide is finer, the transformation quantity of residual austenite is improved, the time is shorter, microscopic plastic deformation is generated inside a sample through the circulation effect of cold and hot media, residual stress opposite to that in the original quenching process is generated, and the reduction effect of the residual stress is better.
5. In the final tempering stage of the heat treatment technology, because micro internal stress generated by the difference of chemical components and structures among areas can cause different thermal contraction in the process of converting the residual austenite to martensite in the cryogenic treatment process, the existence of the micro internal stress promotes the generation of crystal defects such as dislocation, twin crystal and the like, carbon atoms and alloy elements can be segregated at the defect positions to form carbon segregation and become nucleation particles for separating out carbide in the subsequent tempering process, the carbide is dispersed and distributed in an alpha-Fe matrix, the carbide in the matrix is separated out finely in the temperature raising process, the martensite tetragonality is lost, and the residual stress is released.
Drawings
FIG. 1 is a process flow diagram of the present invention.
In the figure: ac of3-austenitizing temperature; mS-a martensite start temperature; t ist-tempering temperature; t ish-temperature of the thermal medium; t isr-room temperature; t isd-cryogenic treatment temperature.
Detailed Description
The present invention will be described in further detail with reference to examples and comparative examples of conventional processes.
Example 1
The technological process of the invention is shown in figure 1, and adopts 4mm thick alloy componentsFe-0.16C-1.2Si-1.7Mn (mass fraction%). Firstly, putting a steel plate into a 980 ℃ air furnace for austenitizing, and preserving heat for 15 min; then putting the mixture into a salt quenching furnace with the temperature of 320 ℃ for salt bath quenching, preserving the heat for 10-15 s, increasing the temperature to 400 ℃, preserving the heat for 240s, performing a carbon distribution process, simultaneously performing vibration treatment by using a vibration exciter, and performing vibration treatment according to a formula sigmadAexp (B/T) ± 5, 95 for a, 14.6 for B, selected dynamic stress σdQuenching with water to room temperature under 99 Mpa; then carrying out deep cooling treatment on the steel plate, preserving heat for 2 hours, taking out the steel plate, placing the steel plate in a heat medium at 200 ℃ for preserving heat for a period of time, and repeating the process once again; and finally, tempering at 400 ℃ for 1 h. The measured values of the residual stress and the reduction rate of the hot rolled steel strip after the treatment are shown in Table 1.
Example 2
The hot-rolled strip steel with the thickness of 4mm and the alloy component Fe-0.16C-1.2Si-1.7Mn (mass fraction%) is adopted. Firstly, putting a steel plate into a 980 ℃ air furnace for austenitizing, and preserving heat for 15 min; then putting the mixture into a salt quenching furnace with the temperature of 360 ℃ for salt bath quenching, preserving heat for 10-15 s, increasing the temperature to 420 ℃, preserving heat for 300s, performing a carbon distribution process, simultaneously performing vibration treatment by using a vibration exciter, and performing vibration treatment according to a formula sigmadAexp (B/T) ± 5, 95 for a, 14.6 for B, selected dynamic stress σdQuenching with water to room temperature under 98 Mpa; then carrying out deep cooling treatment on the steel plate, preserving heat for 2 hours, taking out the steel plate, and preserving heat in a heat medium at 200 ℃ for a period of time, and repeating the working procedure once again; and finally, tempering at 400 ℃ for 1 h. The measured values of the residual stress and the reduction rate of the hot rolled steel strip after the treatment are shown in Table 1.
Example 3
The hot-rolled strip steel with the thickness of 8mm and the alloy component Fe-0.1C-0.19Si-1.2Mn (mass fraction%) is adopted. Firstly, putting a steel plate into a 910 ℃ air furnace for austenitizing, and preserving heat for 10 min; then putting the mixture into a salt quenching furnace with the temperature of 400 ℃ for salt bath quenching, preserving the heat for 10-15 s, increasing the temperature to 470 ℃, preserving the heat for 240s, performing a carbon distribution process, simultaneously performing vibration treatment by using a vibration exciter, and performing vibration treatment according to a formulaσdAexp (B/T) ± 5, a 80, B12.8, selected dynamic stress σdQuenching with water to room temperature at 84 Mpa; then carrying out deep cooling treatment on the steel plate, preserving heat for 2 hours, taking out the steel plate, and preserving heat in a heat medium at 200 ℃ for a period of time, and repeating the working procedure once again; and finally, tempering at 470 ℃ for 1 h. The measured values of the residual stress and the reduction rate of the hot rolled steel strip after the treatment are shown in Table 1.
Example 4
The hot-rolled strip steel with the thickness of 10mm and the alloy component Fe-0.14C-0.1Si-0.5Mn (mass fraction%) is adopted. Firstly, putting a steel plate into a 900 ℃ air furnace for austenitizing, and preserving heat for 10 min; then putting the mixture into a salt quenching furnace with the temperature of 380 ℃ for salt bath quenching, preserving the heat for 10-15 s, increasing the temperature to 480 ℃, preserving the heat for 240s, performing a carbon distribution process, simultaneously performing vibration treatment by using a vibration exciter, and performing vibration treatment according to a formula sigmad(B/T) ± 5, A is 61, B is 15.1, and the selected dynamic stress σdQuenching with water to room temperature at 62 Mpa; then carrying out deep cooling treatment on the steel plate, preserving heat for 2 hours, taking out the steel plate, and preserving heat in a heat medium at 200 ℃ for a period of time, and repeating the working procedure once again; and finally, tempering at 470 ℃ for 1 h. The measured values of the residual stress and the reduction rate of the hot rolled steel strip after the treatment are shown in Table 1.
Comparative example 1
The hot-rolled strip steel with the thickness of 4mm and the alloy component Fe-0.16C-1.2Si-1.7Mn (mass fraction%) is adopted. Firstly, putting a steel plate into a 980 ℃ air furnace for austenitizing, and preserving heat for 15 min; then the steel plate is directly water-quenched to room temperature, and then is tempered at 400 ℃, and the temperature is kept for 2 h. The measured values of the residual stress of the hot rolled strip after the treatment and the reduction rate are shown in Table 1.
Comparative example 2
The hot-rolled strip steel with the thickness of 4mm and the alloy component Fe-0.16C-1.2Si-1.7Mn (mass fraction%) is adopted. Firstly, putting a sample into a 980 ℃ air furnace for austenitizing, and preserving heat for 15 min; then putting the steel plate into a salt quenching furnace with the temperature of 360 ℃ for salt bath quenching, preserving the heat for 10-15 s, then increasing the temperature to 420 ℃, preserving the heat for 300s, and carrying out a carbon distribution process; and finally, tempering the sample at 400 ℃ for 2 h. The measured values of the residual stress and the reduction rate of the hot rolled steel strip after the treatment are shown in Table 1.
Comparative example 3
A hot-rolled strip steel with a sample thickness of 4mm and an alloy component Fe-0.16C-1.2Si-1.7Mn (mass fraction%) is adopted. Firstly, putting a sample into a 980 ℃ air furnace for austenitizing, and preserving heat for 15 min; then, water quenching the steel plate to room temperature, carrying out cryogenic treatment on the steel plate, and keeping the temperature for 12 hours; and finally, tempering at 400 ℃ for 2 h. The measured values of the residual stress and the reduction rate of the hot rolled steel strip after the treatment are shown in Table 1.
TABLE 1
| Examples | Residual stress value before treatment (Mpa) | Residual stress value (MPa) after treatment | Rate of decrease (%) |
| 1 | 257.8 | -75 | 70.6 |
| 2 | 257.8 | -62.4 | 75.8 |
| 3 | 186.3 | -64.3 | 65.5 |
| 4 | 135.6 | -48.8 | 64 |
| Comparative example | Residual stress value before treatment (Mpa) | Residual stress value (MPa) after treatment | Rate of decrease (%) |
| 1 | 257.8 | 206.2 | 20 |
| 2 | 257.8 | 162.4 | 37 |
| 3 | 257.8 | -129.7 | 49.7 |
。
Claims (2)
1. A heat treatment method for reducing residual stress of hot-rolled strip steel comprises the following elements in percentage by mass: 0.06-0.30%, Si: 0.1% -1.5%, Mn: 0.4% -2.0%, Cr: 0.01% -0.1%, Ti: 0.02% -0.12%, Ni: 0.01-0.03%, and the balance of Fe, trace elements B, V, Mo, S, P and other inevitable impurity elements, and is characterized by comprising the following steps:
step one salt bath quenching treatment
Heating the hot-rolled strip steel to a temperature above an Ac3 temperature line, and after the steel plate is completely austenitized, performing salt bath quenching treatment on the steel plate, wherein the temperature is kept below an Ms temperature line; austenitizing the steel plate at 900-1000 ℃, keeping the temperature for 5-20 min, maintaining the salt bath quenching at 300-400 ℃, and keeping the temperature for 5-25 s;
step two carbon distribution-vibration treatment
Heating the temperature to be above the Ms temperature line, performing carbon distribution, simultaneously performing vibration treatment on the carbon distribution by using a vibration exciter, and then performing water quenching to room temperature; the temperature during carbon distribution is 400-500 ℃, the heat preservation time is 200-300 s, the vibration exciter is used for carrying out vibration treatment on the carbon distribution, and the dynamic stress value sigma provided by the vibration exciterdComprises the following steps:
σd=Aexp（B/T）±5
wherein T is the temperature of a medium where the steel plate is located during vibration, A, B is a coefficient, A ranges from 43 to 150, B ranges from 10 to 16, and the yield strength of the material at room temperature is not less than 900Mpa and not less than sigmasThe hot rolled strip steel is more than or equal to 350Mpa, and the vibration temperature T is less than or equal to 560 ℃;
three-step cold and hot circulation treatment
Placing the steel plate obtained in the step two into a cooling medium for cryogenic treatment, then taking out the steel plate, placing the steel plate into a heat medium for heat preservation, and repeating the steps once; the steel plate is reduced to the range of minus 160 ℃ to minus 196 ℃ at the speed of 3 ℃/min to 5 ℃/min, the temperature is kept for 1h to 2h, then the steel plate is taken out and kept in an air furnace for 30 min to 60min at the temperature of 150 ℃ to 250 ℃;
step four tempering
Putting the steel plate obtained in the third step into a heat medium for tempering treatment to obtain a final product; tempering the steel plate, wherein the temperature preservation interval is 250-500 ℃, and the temperature preservation time is 1-2 h.
2. The heat treatment method for reducing the residual stress of the hot-rolled strip steel according to claim 1, wherein the heat treatment method comprises the following steps: the cooling medium used for the cryogenic treatment is at least one selected from liquid nitrogen and dry ice.
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| CN111546069B (en) * | 2020-05-11 | 2021-06-29 | 江苏联峰实业有限公司 | Residual stress eliminating method for hot-rolled high-strength steel |
| CN113073182B (en) * | 2021-03-11 | 2022-08-23 | 南通大学 | Processing method for improving comprehensive performance of E690 high-strength steel for maritime work |
| CN113957298B (en) * | 2021-10-26 | 2022-04-08 | 山东省科学院新材料研究所 | Preparation method of low-residual-stress diamond particle reinforced aluminum matrix composite material |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20020016245A (en) * | 2000-08-25 | 2002-03-04 | 신현준 | Ultra low temperature heat treatment apparatus |
| CN102337385A (en) * | 2011-09-14 | 2012-02-01 | 上海交通大学 | Multi-cycle quenching-partitioning-tempering (M Q-P-T) technique |
| CN102799729A (en) * | 2012-07-13 | 2012-11-28 | 北京航空航天大学 | Effective method for quickly eliminating residual stress of heterogeneous component |
| CN105950856A (en) * | 2016-06-27 | 2016-09-21 | 北京航空航天大学 | Thermal vibration composite device for homogenizing of local residual stress of large ring rolling part |
| CN108531836A (en) * | 2018-05-09 | 2018-09-14 | 湖南人文科技学院 | A kind of heat treatment technics preparing the low residual stress aluminium alloy of high-performance |
-
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- 2019-11-28 CN CN201911186090.7A patent/CN110699605B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20020016245A (en) * | 2000-08-25 | 2002-03-04 | 신현준 | Ultra low temperature heat treatment apparatus |
| CN102337385A (en) * | 2011-09-14 | 2012-02-01 | 上海交通大学 | Multi-cycle quenching-partitioning-tempering (M Q-P-T) technique |
| CN102799729A (en) * | 2012-07-13 | 2012-11-28 | 北京航空航天大学 | Effective method for quickly eliminating residual stress of heterogeneous component |
| CN105950856A (en) * | 2016-06-27 | 2016-09-21 | 北京航空航天大学 | Thermal vibration composite device for homogenizing of local residual stress of large ring rolling part |
| CN108531836A (en) * | 2018-05-09 | 2018-09-14 | 湖南人文科技学院 | A kind of heat treatment technics preparing the low residual stress aluminium alloy of high-performance |
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